Preparation of new surface coating based on modified oil-based polymers blended with ZnO and CuZnO NPs for steel protection

In our paper, we have synthesized modified PEA and alkyd resin by replacing the new source of polyol (SDEA) which was confirmed by different analyses such as IR, and 1HNMR spectra. A series of conformal, novel, low-cost, and eco-friendly hyperbranched modified alkyd and PEA resins were fabricated with bio ZnO, CuO/ZnO) NPs through an ex-situ method for mechanical and anticorrosive coatings. The synthesized biometal oxides NPs and its composite modified alkyd and PEA were confirmed by FTIR, SEM with EDEX, TEM, and TGA, and can be stably dispersed into modified alkyd and PEA resins at a low weight fraction of 1%. The nanocomposite coating was also subjected to various tests to determine their surface adhesion, which ranged from (4B-5B), physico-mechanical characteristics such as scratch hardness, which improved from < 1.5 to > 2 kg, gloss (100–135) Specific gravity (0.92–0.96) and also chemical resistance test which passed for water, acid, and solvent except alkali, was poor because of the hydrolyzable ester group in the alkyd and PEA resins. The anti-corrosive features of the nanocomposites were investigated through salt spray tests in 5 wt % NaCl. The results indicate that well-dispersed bio ZnO and CuO/ZnO) NPs (1.0%) in the interior of the hyperbranched alkyd and PEA matrix improve the durability and anticorrosive attributes of the composites, such as degree of rusting, which ranged from 5 to 9, blistering size ranged from 6 to 9, and finally, scribe failure, which ranged from 6 to 9 mm. Thus, they exhibit potential applications in eco- friendly surface coatings. The anticorrosion mechanisms of the nanocomposite alkyd and PEA coating were attributed to the synergistic effect of bio ZnO and (CuO/ZnO) NPs and the prepared modified resins are highly rich in nitrogen elements, which might be regarded as a physical barrier layer for steel substrates.

Nanocomposite coatings are a new class of coatings made to provide smart, affordable, and efficient surface coatings with exceptional characteristics for applications such as corrosion resistance, antimicrobial protection, antifogging, and adhesives 1,2 . Nanocomposite coatings are usually preferable to traditional coatings due to their improved morphology and phase-separated nanoscale domains 3 . Nanostructured filler particles are spread throughout a matrix to create a nanocomposite coating. The chemical nature of the phases, their relative proportions, and the size of the filler all affect the properties of nanocomposite coatings 4 . Nanoparticle type, shape, size, surface area, percentage of nanofillers, and interactions between the nanoparticles and polymer matrix all have a significant role in the features of nanocomposite coatings 5,6 . The best corrosion resistance may be achieved by evenly dispersing nanoparticles inside the polymer matrix. There are several production techniques and physical, chemical, and mechanical surface treatments that can be used to accomplish this 7 . The polyesteramide hyperbranched polymer-modified nano clay structure demonstrated reduced water permeability and improved corrosion resistance 8 . By adding nanomaterial fillers to polymer matrices, several properties, including stiffness, strength, corrosion resistance, and water resistance, may be enhanced 9 . A nanostructured chitosan/ZnO coating was demonstrated to prevent corrosion on mild steel, with corrosion resistance increasing as the chitosan/ZnO layer was raised. A chitosan and graphene oxide nanocomposite coating that had been modified by oleic acid increased corrosion resistance by a factor of 100 in NaCl solution. The improvement in corrosion resistance  24,30 . The preparation involved two steps.
Step 1: For the preparation of monoglyceride (HESA), DEA (0.5 mol, 52.5 g), Sunflower oil fatty acid (0.5 mol, 140 g), and xylene (50 mL) were mixed in a round-bottomed flask fitted with Dean & Stark to remove the all produced water.
Step 2: the preparation of SDEA-modified PEA resin was carried out as shown in Fig. 2, by partial replacement of Glycerol (Glyc) with SDEA as the source of the polyol, while Phthalic anhydride (PA) is the source of the polybasic acid, in the presence of 10% xylene by volume. The whole ingredients were placed in a 250 mL round-bottomed flask fitted with Dean & Stark. It should be emphasized that for each set of formulations, the total number of hydroxyl and acid equivalents for different runs was kept constant, and the partial replacement of glycerol with SDEA was done. Additionally, the computation of the water freed can be a helpful tool for monitoring the esterification process to establish the theoretical yield reflected in Tables 1 and 2. Cobalt, zirconium, and calcium octoates were added at concentrations of 0.04, 1.0, and 0.05% based on the metal/solid resin, respectively. IR (KBr): ν max (cm −1 ) = 3348 (OH), 2951 (aliph. CH), 1628 (CON), 1585 aromatic C=C stretching frequency, 760 (Ring stretching vibration of aromatic nuclei). 1 HNMR (δ, ppm) = 3.491 the presence of CH 2 peaks attached to free hydroxyl, with amide nitrogen and amide carbonyl peaks present at 3.491 ppm, 3.56-3.745 ppm and 2.6-3.0 ppm respectively, 5.5 existence of OH peaks, 7.0-8.0 peaks present in the aromatic region 31 .    Preparation of bio CuO/ZnO nanocomposite modified PEA, and bio ZnO nanocomposite modified Alkyd and their incorporation with a high gloss paint formulation. The prepared modified polyesteramide resin and alkyd resin (80 wt% solid content) were mixed individually with 10 wt% xylene and turpentine (1:1) mixing ratio.
The desired amount of driers, including Co, Mn, and Ca octoate as a mixed driers solutions, were added by weight of the total formulation, respectively. These driers were mixed under constant stirring to produce homogeneous solutions. Two types of nanoparticles, bio CuO/ZnO and bio ZnO have been selected and used in a concentration of 0.1 wt% to prepare the nanocomposite-modified PEA and alkyd, the prepared nanocomposites were cured using the solution casting technique. CuO/ZnO, ZnO nanospheres of a concentration of 0.1% were sonicated for 15 min. in a mixture of turpentine and methylbenzene (1:1 by volume). The modified PEA and/ or modified alkyd resin (80 wt% solid content to (0.1%) wt% CuO/ZnO and/or bio ZnO nanosphere solution) was solubilized in 10 wt% of the utilized solvent under continuous stirring 42 . The process is simplified in Fig. 5. www.nature.com/scientificreports/ After the preparation of nanocomposite resins, the prepared nanocomposite modified resins were added to the paint formulation to create the high gloss coating compositions. Table 3 lists the ingredients in the produced paint formulation either based nanocomposite modified PEA and/or based on bio ZnO nanocomposite modified alkyd resins. The steps of the process have been presented in Table 3, and presented in Fig. 5. The prepared coating formulation' compositions were applied to steel panels using a brush. Every effort was made to keep the dry film thickness at around 120 + or − 5 µm 27,35-37,43,44,45 . Characterization. Bruker FT-IR analyzer. IR Spectra were determined using KBr-disk technique on a Shimadzu 440 spectrophotometer within the range of 400-4000 cm −1 .
Degree of polymerization (DP). The acid value, (an industrial measurement for the conversion that can be obtained by titrating with potassium hydroxide solution in ethanol), was served as a representation of the DP of the resins (KOH) ASTM D1980-87(1998) 46 .
Thermal analysis. Thermogravimetry analysis of the coated sample was carried out using a TGA instrument (STA model 650) with a heating rate of 20 °C/min in a 45-950 °C temperature range.
Scanning electron microscopy (SEM). Surface morphologies of the prepared nanocomposite and coated samples were observed with a scanning electron microscope (SEM, Joel Jsm 6360LA-Japan).
Transmission electron microscopy (TEM). Samples were observed under transmission electron microscopy (TEM) on JEOL (GEM-1010) at an operating voltage of 76 kV.
Method of testing and evaluation. All resins were adjusted to a solid content = 60% (according to ASTM Method, D1644-01, (Reapproved 2012), and the performance film properties were examined using the following test methods: the preparation of the steel panels D609-17; measurement of film thickness according to ASTM method D1005-13. The specular gloss measurements were performed according to ASTM method D523-18, and film hardness was measured using a pencil hardness tester according to ASTM method D3363-11. Finally, adhesion was tested using a cross-hatch cutter, according to ASTM method D3359-17, and flexibility was determined as per the ASTM method D522-17.
Anticorrosive studies. The salt spray test was used to determine the corrosion resistance of the painted panels. The guidelines and test procedures are described in the international standard ASTM B117. 39 The salt fog solution consists of sodium chloride (5%wt). The nano-coated surfaces were exposed to a C&W salt fog cabi-  1 HNMR (δ, ppm) = Characteristic peaks for chain -CH 2 -appears at δ = 1.14-1.99 and terminal -CH 3 appears at δ = 0.84 ppm. The peaks of CH 2 attached to amide carbonyl (> N-(C=O)-CH 2 ) at δ 4.5 ppm, and amide nitrogen ((-CH 2 ) 2 N-C=O) at δ 3.5 ppm. The peaks for protons of the -CH=CH moiety appear at δ 5.29-5.31 ppm. The proton of the phthalic moiety's aromatic ring and the proton of the xylene moiety's aromatic ring at a concentration between 6.9 and 7.9 ppm 31 .
Spectral analysis of SDEA-modified alkyd resin. Alkyd resin's structural characteristics were investigated using FT-IR shown in S (5) and 1 HNMR in S (6). IR (KBr): ν max (cm −1 ) = 3446 (OH), 3008(arom. CH), 2927 ((C-H) CH 2 asymmetric stretching), 2855 ((C-H) CH2 symmetric stretching), 1738(COO stretching of ester linkages), 3009(arom. CH), 1599 (stretching frequency of alkene and aromatic band), 746 (Ring stretching vibration of aromatic nuclei). 1 HNMR (δ, ppm) = Characteristic peaks at δ = 0.8-0.9 due to terminal -CH 3 group, peaks at δ = 1.15-154 ppm. Due to the protons of CH 2 groups attached next to the above terminal methyl group. Peaks at δ = 2.00-2.76 ppm for CH 2 of double allylic protons. Characteristic peaks at δ = 4.14-4.39 ppm is for protons of the glyceride moiety, and the peak at δ = 5.33 ppm is due to existence of OH peaks, the peaks for protons of the -CH=CH moiety appear at δ = 6.75-6.99 ppm, at δ = 7.125-7.85 ppm are observed for aromatic protons of PA containing resins. (7) shows the ZnO NPs FT-IR spectrum. The sample has absorption peaks in the range of 800-1600 cm −1 , which are connected to the presence of organic chemicals. The amide group's C=O stretching vibration band and the existence of COOH and OH groups are shown by the peaks' absorption at 1630 and 3437 cm −1 , respectively 37 . The -CH 2 and C-C bonds in the aromatic ring are responsible for peaks at 2920 and 1411 cm −1 , respectively. The peak absorption at 1630 cm −1 can also result from stretching vibrations of C=O. A peak at 1039 cm −1 also suggests the presence of phenol, alcohol, and amines (aliphatic). The phenols in the capping agent link to the surface of ZnO to create ZnO NPs, while the C=O, C-O=C, and C=C groups of heterocyclic compounds may serve as stabilizers 38,39 . Because the peaks in the region between 500 and 900 cm −1 are ascribed to metal-oxide (M-O) bonds, the FT-IR spectrum then absorbs the peak at 875 cm −1 , indicating the stretching vibrations of ZnO 40 .

Morphological analysis.
To study the morphology of ZnO NPs, SEM measurements were carried out. The SEM micrographs depicted in Fig. 6A show how the obtained ZnO NPs are approximately spherical in form with aggregation as a result of their interaction with water and the intramolecular Van-der Waals, magnetic, and electrostatic interactions. TEM proved the homogeneity and nanoscale of ZnO NPs. The form the nanoparticles generated is of a spherical type with an average size found to be 20-40 nm as indicated in Fig. 6B.  27 , whereas that at 864 cm −1 may be is ascribed to CH and CC of alkene 56 .
Scanning electron microscopy (SEM). SEM was utilized to analyze the surface morphology of the biosynthesized NPs as seen in Fig. 7A; the result proved almost spherical NPs with few agglomerations. These agglomerations may be linked to NPs' increased propensity for forming huge clusters 57 .    Figure 8 shows SEM images illustrating the states of sample blank PEA and alkyd without modification Fig. 8A and bio CuO/ZnO NPs in the PEA resin Fig. 8B and bio ZnO NPs in the alkyd resin Fig. 8C of to form nanocomposite modified polymers. It's observed that there's good roughness for all the samples, either for sample blanks of PEA and alkyd resin or for modified PEA and alkyd nanocomposite. Although the level of roughness was not uniform throughout the sample, it was visible for the good loadings of the proportion of modified nanocomposite PEA and alkyd; also, the images indicated that there's no agglomeration, and performance and dispersion were good.
Characterization of prepared paint formulation based on nanocomposite. Thermal analysis. Thermal analysis of paint based on bio CuO/ZnO nanocomposite modified PEA. Figure 9 shows TGA of dry coating based on CuO/ZnO nanocomposite-modified PEA sample. The TGA curve of this sample shows  www.nature.com/scientificreports/ four distinct weight loss steps, consistent with the results reported for nanocomposite coating 31 . The coated sample's DTG curve shows four peaks that correlate to different stages of weight loss. The first step in the weight loss in TGA curve and the associated first peak in DTG curve at 388 °C are caused by the decomposition of the aliphatic diol portion (HESA) in the polyesteramide and adsorbed solvent and reacted moieties 31 . The second step of weight loss and the associated second peak at 489.87 °C is caused by the decomposition of ester, ether, and unsaturated bonds and ester amide moieties present in the coating matrix 25,31 . The third weight loss step and the corresponding third peak at 697 °C may be attributed to the decomposition of CuO/ZnO composite modified PEA into the coating matrix 58 . The fourth weight loss step and the related fourth peak at 801 °C may be the cause of the decomposition of some fillers in the coating formulation, such as calcium carbonate, which is converted into calcium oxide (CaO), and also, TiO 2 . Therefore, the high compatibility between the nanocomposite-modified resin and the solid materials in the coating formulation and the good dispersion. So, the obtained results of the thermal gravimetric stability indicated that the final product of the coating based on CuO/ZnO modified PEA has good thermal stability because of the introduced nanocomposite binder, nitrogen elements in the polymer structure, and finally, the high compatibility and high dispersion of the components of the coating formulation.
Thermal analysis of paint based on bio ZnO nanocomposite modified alkyd resin. Figure 10 shows the similar behaviour of TGA and derivative thermogravimetry analysis (DTG) curves for dry coating based on CuO/ ZnO nanocomposite-modified PEA and bio ZnO nanocomposite-modified alkyd samples. But there are a few differences between each of them, because of the presence of nitrogen element which is repeated in the polyesteramide and introduced in CuO/ZnO Np, which combines the advantage of Cu and the advantage of Zn, So, all of these encourage the enhancement of the high thermal stability of these types of coatings. So, we can notice from Figs. 9 and 10 that the obtained results of the dry coating based on CuO/ZnO nanocomposite-modified PEA were more thermally stable than those of the dry coating based on bio ZnO nanocomposite-modified alkyd resin. The coated sample's DTG curve shows four peaks that correlate to different stages of weight reduction. The initial step in the TGA curve's weight loss and the matching first peak in the DTG curve at 31 °C result from the decomposition of the aliphatic diol portion (HESA) in the modified alkyd and adsorbed solvent and reacted moieties 31 . The second stage of weight loss and a subsequent second peak at 486 °C are caused by the decomposition of ester, ether, and unsaturated bonds present in the coating matrix 25,31 . The third stage of weight loss and subsequent third peak at 654.11 °C might be attributable to the decomposition of bio ZnO composite modified alkyd resin into the coating matrix 58 . The fourth weight loss step and the fourth peak at 720 °C might be a result of the decomposition of some fillers in the coating formulation, such as calcium carbonate, which is converted into calcium oxide (CaO), and, TiO 2 . Thus, the high compatibility between the nanocomposite-modified alkyd resin and the solid materials in the coating formulation and the good dispersion. So, the obtained results of the thermal gravimetric stability indicated that the final product of the coating based on bio ZnO-modified alkyd is a good thermally stable. Coating characteristics of cured modified resins. Mechanical characteristics. We can see from the data shown in Table 4 that the mechanical characteristics of curing panels of modified PEA and alkyd resins were similar in the results that were obtained. The existence of salicylic diethanolamine as a modifier led to  www.nature.com/scientificreports/ significantly improved physio-mechanical characteristics such as scratch hardness, gloss, adhesion, and thermal stability. It was noticed that in the case of coated films based on modified PEA, the mechanical properties were improved more than those based on modified alkyd, and this may be due to the presence of nitrogen element in the PEA. Fatty acids undergo an oxidative cross-linking process, which causes PEA and alkyd coating films to dry. So, as shown in Table 4. The drying time in the stove increases from 2-3 h at 150 °C and this may be owing to the fact that with the increase of the fatty acid content in the resin, the unsaturation part degree was not enough to oxidize, so it required more than 2 h to be hard dry films if they were compared to blank samples of PEA and alkyd resins. The stiff aromatic moiety in the polymer chain is responsible for the increased pencil hardness rating. The hardness value for resins is also increased by the addition of SDEA 35 . The bend test reveals that cross-linked networks have excellent flexibility. Alkyd resins pass the bend test and have strong adhesion qualities because they contain polar ester linkages, either in PEA or in alkyd resins. Table 4 shows that the other important properties like adhesion and gloss of modified PEA and alkyd resins were also enhanced by boosting the replacement in PEA and alkyd. The resin's adhesion was enhanced because of the existence of polar ester bonds. Gloss is enhanced due to the presence of the aromatic PA moiety and the novel modifier (SDEA) in PEA and alkyd resin. All of the resin's gloss properties may be rated as good [24][25][26][27][28][29][30][31][32][33][34][35][36][37][43][44][45]48,59 .
Chemical resistance of dry-coated films. Table 5 lists the resin's film performance in various chemical conditions. All samples of modified and nanocomposite resins had chemical resistance characteristics comparable to the reference sample of PEA, and all resins' alkyd films have excellent water resistance, acid, and solvent resistance except for alkali. The modified resin is fairly resistant to alkali than blank sample, maybe as a result of the PA's abundant stiff aromatic moiety and the content of SDEA in the structure of prepared resins, which increases by increasing the replacement. As a result of the presence of an alkali hydrolyzable ester group, the alkali resistance drops [24][25][26][27][28][29][30][31][32][33][34][35][36][37][43][44][45]48,59 . The chemical resistances of the unmodified PEA and unmodified alkyd-cured films and nanocomposites were evaluated in comparison to several solutions, including Na 2 CO 3 , H 2 O, and H 2 SO 4 in Table 5. Applying the coatings to the glass plates allowed for the evaluation of the films' chemical resistance. Plates were then cured for 48 h by being submerged in various solutions and solvents. To stop solvent from penetrating between the plate and the coating, the edges of the plates were coated with paraffin wax. The plates were evaluated and examined for any signs of changes to the coated resins. Comparing the nanocomposite films to unmodified PEA and alkyd films, the nanocomposite films showed greater resistivity and indicated higher resistance in acid solutions. To investigate the coatings' acid stability, an H 2 SO 4 solution was used. The films demonstrated good resistance to acid. All the films that had been immersed in the H 2 SO 4 solution afterward showed gloss loss and color changes. The films of unmodified alkyd then blistered, but the films of modified PEA and modified alkyd simply shrank and continued to be acid resistant. Using a 5 wt.% Na 2 CO 3 solution, the alkali resistance of coatings was evaluated. Within 48 h of soaking, the changes in the coated plates were noticeable. Within two days, all films of unmodified and modified PEA and modified alkyd were removed entirely. The hydrolyzable ester linkages in the PEA and alkyd resin chains were likely the source of the low resistance of alkyd films and their nanocomposites   60,61 . Glass plates with coatings that were submerged in distilled water exhibited no change. This is explained by their elevated hydrophobicity. The results of the chemical resistance tests of all samples of coated films made from modified PEA and modified alkyd resin are summarized in Table 5 and are identical.
Testing corrosion resistance of the coating. Table 6 contains measurements and statistics related to salt spray. Once the films failed to adhere, the salt spray test was discontinued. Figures 13 and 14 illustrate the salt spray test findings with pictures of dried paints made from PEA and alkyd modified with nanocomposite materials. The findings of the salt spray showed that the steel substrate painted with the primer based on bio CuO/ZnO and bio ZnO nanocomposite modified PEA and alkyd resin had excellent adhesion. This was seen in the PEA and alkyd modified with nanocomposite coatings that performed better after 450 h of exposure to the salt spray environment compared with the sample blank. For every coating exposure time, coating performance was continuously increased. Relationships between coating characteristics and performance can be credited with Coating based on bio CuO/ZnO nanocomposite poly(ester-amide) resin 9 9 Medium dense 9 www.nature.com/scientificreports/ this. In this regard, the primary cause of coating failure is the substrate's adhesion to the coat. Strong adhesion also stops moisture vapor from penetrating the coating and condensing in an area with low adhesion, which would otherwise cause the coating to blister. This is especially important when choosing the appropriate coating systems. In this work, it was observed that increasing the amount of SDEA in the modified PEA and alkyd resins and the hydroxyl contents of cured PEA and alkyd resins also increased the adhesion of the coat to steel. It has been shown that the nonmodified resins and nanocomposites with the PEA and alkyd have a non-positive effect on the adhesion of the alkyd coating to the steel metal. So, it was affected when exposed to the salt spray 33 .
Hyperbranched alkyd matrices have stronger anticorrosive protection than regular matrices, according to prior investigations 58 . A traditional alkyd matrix was prepared with reduced resistance to NaOH solution, and the manufactured coating layers were totally separated 60 . According to the tabulated results in Table 6, the corrosion spread of steel-painted panels based on unmodified PEA and alkyd was greater than that of PEA nanocomposite CuO/ZnO and nanocomposite bio ZnO alkyd, which was approximately 1.5-2 mm; in the case of steel painted panels based on PEA nanocomposite bio CuO/ZnO, the corrosion resistance was higher than that of nanocomposite bio ZnO alkyd. This finding reflects the effects of the distribution of the bio nano CuO/ZnO and bio ZnO nanocomposite modified alkyd on corrosion protection. The gradual insertion of nano-CuO/ZnO and also ZnO decreases the density of blisters and the rusting of spots compared with the painted steel panel based on unmodified PEA and alkyd. From the obtained results of the corrosion resistance, we can conclude that the improvements may be achieved by evenly dispersing nanoparticles inside the polymer matrix, resulting in improved adhesion to the substrate 62 . And the introduction of the nitrogen element into the PEA structure Also, the protection of mild steel from corrosion is attributed to its being impermeable to water and corrosive ions and having reduced water permeability 25 .
Mechanism of corrosion protection. The mechanism of protecting bio ZnO, CuO/ZnO nanocomposite PEA and alkyd coated mild steel substrate against corrosion through electrostatic repulsion of chloride species is shown in the schematic in Fig. 13. It is depicted in this schematic that after making cross-cut along with the coatings, created microcavities on the coating surfaces when exposed to saline and foggy environment for better understanding of the corrosion inhibition property during the corrosion test of the unmodified and modified nanocomposite PEA and alkyd coating. These cavities allowed the ingress of the corrosive solution to the coating-metal interface. In the bio ZnO, CuO/ZnO nanocomposite PEA and alkyd coatings, chloride ions were restricted by bio ZnO, CuO/ZnO nanocomposite PEA and alkyd through electrostatic repulsion, comparing with the coated steel panel based on unmodified alkyd and PEA resins, which did not hinder or restrict the ingress of neutral species (oxygen and water) through the cavities on the coating surface. Over time, oxygen and water diffused into the coating-metal interface to initiate uniform corrosion by the formation of ferrous hydroxide as follows. This repulsion of chlorides prevented chloride-initiated corrosion at the coating-metal interface as shown in Fig. 14 63 .
With more oxygen diffusion into the coating, ferrous hydroxide is converted to ferric oxide, indicated as deep brown in schematic (a). This conversion can be described thus: However, in schematic Fig. 13B and C, the mild steel-coated bio nanocomposite coating samples exhibited severe pitting attacks following weak electrostatic repulsion of the chloride ions. Unlike the unmodified coated samples. Hence, the repulsion of chloride ions was ineffective for the coated sample based on nanocompositemodified alkyd and PEA, compared to the unmodified coatings, leading to corrosion at the coating-metal interface of the coated sample based on unmodified alkyd and PEA Fig. 13A.
The pits initiation by chloride ions at the interface starts with the formation of ferrous cations according to the following two reactions 64 : The presence of water and oxygen causes the oxidation of iron to ferrous hydroxide, The ferrous hydroxide further combined with the ferrous chloride as the following: Moreover, the improvement of anticorrosion performance using ZnO, CuO/ZnO nanocomposite coating might be ascribed to the following reasons: (1) the alkyd and poly(ester-amide) coatings might be regarded as a physical barrier layer, (2) the nanoscale ZnO, CuO/ZnO could effectively form a dense passivation film with Fe element, which significantly prevented the corrosive mediums such as water, oxygen, chloride ion from further diffusing into the surface of the mild metal. This was why ZnO, CuO/ZnO nanocomposite coating owned the best anti-corrosion performance compared to other nanocomposite coatings (A,) (blank coating), (3) the nanosheet structure of ZnO, CuO/ZnO nanocomposite coating provided an extra barrier film to significantly prevent the www.nature.com/scientificreports/ water, oxygen, chloride ion from penetrating the pores, thereby preventing the corrosion of the underlying metal, and (4) due to, the well-dispersed ZnO, CuO/ZnO hybrids in alkyd and poly(ester-amide) could enhance the corrosion protection performance of the coatings (5) may be also the improvement due to mixed metal oxide NPs which are composite with highly rich nitrogen-modified binders that provide corrosion protection and prevent anodic corrosion by forming a protective passive layer on the substrate by the delocalized electrons on the nitrogen atoms in addition to the presence of metal nanoparticles 58 . It has been further reported that the modified alkyd and PEA coatings act as an anticorrosive binder e to retain the metal in the passive state 35,44,45 . Further mixed metal oxide nanocomposite such as TiO 2 , Al 2 O 3 , Mn, Co, Cd, Cu and Zn 65-68 alkyd and PEA act as a mediator for anodic current between the passivated mild steel surface and oxygen reduction in the coating. The Fe 2+ formed due to the initial corrosion reaction reacts with the dopant anions generated from nanocomposite alkyd and PEA reduction leading to the formation of insoluble iron-dopant salt which further passivates the mild steel surface along with nanocomposite alkyd and PEA.
SEM of the corrosion resistance of painted steel panels after corrosion. The SEM micrograph, as shown in Fig. 15 of the coated steel panels After corrosion shows a few holes and localized corrosion is apparent, especially for the valleys and defect areas for blank coated steel panels, maybe this is attributed to the presence of agglomeration in the blank coating formulation, which may cause the differences in the coating's surface structure and composition by which the localized corrosion of coatings not based on nanocomposite PEA and alkyd can be induced. While the surfaces of coated steel panels based on CuO/ZnO nanocomposite PEA and coated steel panels based on bio ZnO nanocomposite alkyd are smooth and nearly no obvious holes can be seen, the surface is much smoother than the surface of the blank coating, and this is due to the same reasons mentioned previously, such as the presence of nitrogen elements, and the prepared nanocomposite modified PEA and nanocomposite modified alkyd resin.

Conclusion
In this study, a successful preparation of two new modified PEA and alkyd resins based on sunflower oil fatty acid was achieved. The modification has been done by partial replacement of monoglyceride with salicylic diethanolamine as the ingredient source of polyol. The FTIR and 1 HNMR spectra confirmed the chemical structures of both the new polyol and the resins with the functional groups present. The green nano-biosynthesis method was employed to prepare ZnO and CuO/ZnO nanoparticles, which were then incorporated in the modified PEA and alkyd resins. The nanocomposites obtained were characterized by FT-IR, TGA, and SEM. Then, the prepared nanocomposite resins were formulated as binders in paint formulation to be evaluated as anticorrosive resins for steel protection. It was observed that the modified resins, either modified PEA or modified alkyd resins, showed great improvement in overall coating properties compared to other unmodified resins. The existence of salicylic diethanolamine as a modifier led to significantly improved chemical resistance and physio-mechanical properties such as scratch hardness, gloss, adhesion, and thermal stability, but it was noticed that in the case of coated films based on modified PEA, these properties were improved more than those based on modified alkyd and this may be due to the presence of nitrogen elements in the structure of the polymer. Modified nanocomposite binders showed better film performance in terms of corrosion when blended within the paint formulation. The anticorrosive results of the formulated coating revealed that the film-loaded, well-dispersed bio-ZnO and CuO/ ZnO spherical nanofillers had a perfect anticorrosive effect when applied for steel protection.

Data availability
The datasets used and analyzed during the current study are available from the corresponding author upon reasonable request.